Electrocatalytic materials and methods for manufacturing same

ABSTRACT

The present invention provides an electrocatalytic material and a method for making an electrocatalytic material. There is also provided an electrocatalytic material comprising amorphous metal or mixed metal oxides. There is also provided methods of forming an electrocatalyst, comprising an amorphous metal oxide film.

CROSS-REFERENCE TO RELATED APPLICATIONS

This application claims the benefit of U.S. Provisional Application No. 61/530,289 filed on Sep. 1, 2011 and U.S. Provisional Application No. 61/581,303 filed on Dec. 29, 2011, the entire contents of each of which are incorporated herein by reference.

FIELD OF THE INVENTION

The present invention relates to electrocatalytic materials and in particular to amorphous metal oxides and their use as catalysts for water oxidation.

BACKGROUND OF THE INVENTION

Clean renewable sources of energy are required to overcome the rising energy demand of the coming decades. Solar energy can be considered to be a carbon-neutral energy source of sufficient scale to meet future global energy demand. Variability in local insolation, however, requires cost-effective storage of solar energy for its large scale deployment as a primary energy source. In nature, photosynthesis captures sunlight and converts it into a wireless current which is stored. Efforts have been made to duplicate natural photosynthesis in energy conversion systems that capture and convert solar energy.

One of the most promising schemes for the large-scale storage of solar energy is the electrochemical conversion of water—an abundant and noncarbonaceous resource—into dihydrogen and dioxygen fuels. Electrolysis of water, that is, splitting water into oxygen and hydrogen gases, is one such energy conversion process that is not only important for the production of oxygen and/or hydrogen gases, but for energy storage. Energy is consumed in splitting water into hydrogen and oxygen gases and, when hydrogen and oxygen gases are recombined to form water, energy is released.

Electrocatalysts provide low energy activation pathways that permit electricity-producing reactions to occur at a practical rate. In the context of the electrolysis of water, electrocatalysts are required to negotiate the proton-coupled electron-transfer steps and thermodynamic demands associated with the oxidation of water (Equations 1 and 2). 2H₂O

O₂+4e ⁻+4H⁺ E_(anodic)=1.23−0.059(pH)V vs NHE 4e ⁻+4H⁺

2H₂ E_(cathodic)=0.00−0.059(pH)V vs NHE

Crystalline materials have been believed to be effective electrocatalysts as these materials provide the regularity of a crystal lattice that gives rise to a higher conductivity and less charge recombination at defects. U.S. patent application Ser. No. 10/343,272 describes a process involving spray pyrolysis (the use of toxic chemicals and high temperatures) in the preparation of a photocatalytic polycrystalline film of iron oxide.

Amorphous alloys have also been shown to be potentially effective electrocatalytic materials as these materials have shown higher activities and selectivities than their crystalline counterparts for many catalytic transformations. Reasons for the effectiveness of amorphous alloys have been attributed to a greater number of randomly oriented bonds in an amorphous solid relative to a crystalline solid enabling a higher density of coordinated unsaturated sites for the facile adsorption of reactants. As well, the discontinuous nature of amorphous materials can increase the number of edges and terminal oxygens (and thus an enhanced coverage of reactive species) as well as structural flexibility to enhance dioxygen evolution.

U.S. patent application Ser. No. 12/486,694 describes the electrolysis of Co²⁺ in phosphate, methylphosphonate and borate electrolytes to prepare an amorphous highly-active water oxidation catalyst as a thin-film on a current collector.

Despite advances in the development of electrocatalysts, significant market penetration by commercial electrolyzers remains hindered by the absence of a commercially competitive catalytic material that exhibits low overpotentials and high current densities over prolonged time periods. Therefore, a need remains for the development of improved materials and devices that operate with increased energy conversion efficiency.

Further, while dopants, nanostructuring, co-catalysts, atomic layer deposition, and/or plasmonic materials are known to enhance the photocatalytic activity of hematite (an α-ferrous oxide), these methods are cumbersome, expensive and/or lead to variable and undesirable characteristics in the electrocatalyst. Alternate means to optimize the electronic properties of electrocatalysts are desirable.

This background information is provided for the purpose of making known information believed by the applicant to be of possible relevance to the present invention. No admission is necessarily intended, nor should be construed, that any of the preceding information constitutes prior art against the present invention.

SUMMARY OF THE INVENTION

An object of the present invention is to provide an electrocatalytic material and a method for making an electrocatalytic material. In accordance with an aspect of the present invention, there is provided an electrocatalytic material comprising amorphous metal or mixed metal oxides. In accordance with another aspect of the present invention, there is provided a method of forming an electrocatalyst, comprising an amorphous metal oxide film comprising the steps of: providing a substrate; coating the substrate with a metallo-organic precursor solution; converting the metallo-organic precursor to zero oxidation state metal; and oxidizing the zero oxidation state material to a metal oxide to form the amorphous metal oxide film, wherein the metallo-organic precursor solution comprises a precursor selected from the group consisting of an iron precursor, a cobalt precursor, a nickel precursor, and mixtures thereof.

In accordance with another aspect of the present invention, there is provided a method of forming an electrocatalyst comprising an amorphous metal oxide film comprising the steps of: providing a substrate; coating the substrate with a metallo-organic precursor solution; converting the metallo-organic precursor to a prepared state metal; and oxidizing the prepared state material to a metal oxide to form the amorphous metal oxide film.

In accordance with another aspect of the present invention, there is provided a use of a metal oxide film in electrocatalysis. In accordance with another aspect of the present invention, there is provided a system for electrocatalysis comprising an electrocatalytic material comprising an amorphous metal oxide film.

BRIEF DESCRIPTION OF THE DRAWINGS

These and other features of the invention will become more apparent in the following detailed description in which reference is made to the appended drawings.

FIG. 1 presents a schematic of the method for preparing an electrocatalyst, according to an embodiment of the present invention.

FIG. 2 presents a schematic of the method for preparing an electrocatalysts, according to an embodiment of the present invention using an iron (III)-2 alkanoate [Fe(O₂CR)₃], which is converted to ferric oxide during photolysis.

FIG. 3 illustrates the optical characteristics of Fe₂O₃ films.

FIG. 4 illustrates the infrared spectra at various time points during the photolysis of the Fe(III) 2-ethylhexanoate precursor on CsI plates according to one embodiment of the present invention.

FIG. 5 illustrates the x-ray diffraction patterns for prepared Fe₂O₃ films which were annealed at various temperatures according to one embodiment of the present invention.

FIG. 6 is a series of photographs of Fe₂O₃ films which were annealed at various temperatures according to one embodiment of the present invention.

FIG. 7 illustrates the thickness of Fe₂O₃ films as a function of annealing temperature according to one embodiment of the present invention.

FIG. 8 are plots/optical determinations of band gaps (E_(g)) for Fe₂O₃ films according to one embodiment of the present invention.

FIG. 9 is a series of scanning electron micrographs of blank FTO and Fe₂O₃ films according to one embodiment of the present invention.

FIG. 10 are cyclic voltammograms of Fe₂O₃ films on FTO according to one embodiment of the present invention.

FIG. 11 is a plot of the production of O₂ during controlled-potential electrolysis using an a-Fe₂O₃ sample annealed at 250° C. according to one embodiment of the present invention.

FIG. 12 is a plot of the current density as a function of annealing temperature at 1.53 V vs. RHE according to one embodiment of the present invention.

FIG. 13 is a (a) Mott-Schottky plot and (b) a plot of charge carrier density of amorphous metal oxide films in neutral and basic media according to one embodiment of the present invention.

FIG. 14 is a schematic of a photo-electrocatalytic cell for water oxidation according to one embodiment of the invention.

FIG. 15 is UV and visible spectra of (a) iron oxide films, and (b) cobalt oxide films, annealed at various temperatures, according to one embodiment of the present invention.

FIG. 16 is the valence band E_(vb) and conduction band E_(cb) positions plot derived from ultraviolet photoelectron spectroscopic and UV-vis data for iron oxide films annealed at various temperatures, according to one embodiment of the present invention.

FIG. 17 is the cyclic voltammograms studies on (a) iron oxide films, and (b) cobalt oxide films, annealed at various temperatures, according to one embodiment of the present invention.

FIG. 18 is the Tafel plots of (a) iron oxide films, and (b) cobalt oxide films, annealed at various temperatures, according to one embodiment of the present invention.

FIG. 19 is the cyclic voltammograms acquired in light (1 sun equivalent) and dark conditions for (a) a crystalline iron oxide film, and (b) a mixed crystalline and amorphous iron oxide film, according to one embodiment of the present invention.

FIG. 20 is a graph of the chronoamerometry data obtained for a mixed crystalline and amorphous iron oxide film, according to one embodiment of the present invention.

FIG. 21 is a table of current density values (μA/cm²) from chronoamperometry studies of (A1) a film of 5 layers of amorphous iron oxide annealed at 250° C.; (A2) a film of 5 layers of amorphous iron oxide annealed at 400° C.; (C) a film of 5 layers of crystalline iron oxide annealed at 600° C.; and (CA) a film of 4 layers of crystalline iron oxide annealed at 600° C. and one layer of amorphous iron oxide annealed at 250° C.; at difference voltages, in light (1 sun equivalent) and dark conditions, according to one embodiment of the present invention.

FIG. 22 is a series of wide scan survey spectra from XPS studies of as-prepared Fe₂O₃ film, and Fe₂O₃ films annealed at 250° C. and 600° C.

FIG. 23A shows cyclic voltammograms obtained using iridium oxide films produced using three different annealing temperatures, and iridium doped iron oxide films produced at three different annealing temperatures.

FIG. 23B shows cyclic voltammograms obtained using molybdenum oxide films produced using three different annealing temperatures, and molybdenum doped iron oxide films produced at three different annealing temperatures. Cyclic voltammograms obtained using bare FTO electrode (annealed at 300° C.) and iron oxide film (as-prepared) are also included for reference.

FIG. 23C shows cyclic voltammograms obtained using niobium oxide films produced using three different annealing temperature, and niobium doped iron oxide films produced at three different annealing temperatures. Cyclic voltammograms obtained using bare FTO electrode (annealed at 300° C.) and iron oxide film (as-prepared) are also included for reference.

FIG. 24 is the Tafel plots of Fe oxide film, FeCo oxide film and FeCoNi oxide film.

FIG. 25 is the Tafel plots of bare FTO electrode versus iron oxide film.

FIG. 26 is the Tafel plots of FeCoNi oxide film under neutral conditions (0.5M KPi, pH 7.0) and in seawater (pH 8.4).

FIG. 27 is the O₂ production as measured by fluorescent sensor versus theoretical O₂ production.

DETAILED DESCRIPTION OF THE INVENTION

The present invention relates to electrocatalytic materials, a method for preparing electrocatalytic materials, and the use of electrocatalytic materials of the present invention in electrodes, systems, and methods for electrolysis of water and other electrochemical techniques.

The electrocatalytic materials of the present invention comprise metal oxides. In one embodiment, the metal oxides of the electrocatalytic materials comprise amorphous metal oxides. In accordance with the present invention, the metal oxide may comprise the oxide of a single metal selected from, but not limited to iron, cobalt, nickel, ruthenium, platinum, palladium, molybdenum, osmium, manganese, chromium, titanium, rhodium and iridium oxides. In embodiments of the present invention, the metal oxide comprises iron oxide, cobalt oxide, nickel oxide or iridium oxide. The present invention also relates to catalysts comprising mixed metal oxides, including combinations of two, three or more metal oxides in varying proportions. Examples of binary systems that fall within the scope of the present invention include, but are not limited to, iron/cobalt, iron/nickel, cobalt/nickel, cobalt/aluminum, nickel/aluminum, iron/aluminum, iron/cerium, iron/molybdenum, iron/copper, iron/iridium, iron/manganese, iron/tin, and iron/niobium. Examples of ternary systems that fall within the scope of the present invention include, but are not limited to, iron/cobalt/nickel, iron/aluminum/nickel, aluminum/cobalt/nickel, and aluminum/cobalt/iron mixtures. In accordance with one embodiment of the present invention, the catalyst comprises a doped metal oxide, including but not limited to iridium doped iron oxide, molybdenum doped iron oxide, and niobium doped iron oxide.

The electrocatalytic materials of the present invention are prepared by a method involving photochemical metal organic deposition (PMOD) technique. PMOD is a bench-top process that requires neither high vacuum or elevated temperatures; uses simple and benign precursors; and is compatible with a variety of nanostructuring schemes (including imprint lithography, electron-beam patterning, and nanocomposite synthesis). Accordingly, PMOD is a low-cost and scalable technique which is amenable to large-scale production and nanostructuring, for obtaining large-area electrodes. PMOD is also amenable to the deposition of mixed metal oxide films, obtained when two or more precursors are premixed in a precursor solution.

A person skilled in the art will appreciate it is within the scope of the present invention that the electrocatalytic materials, including amorphous metal oxides, may be prepared by other means including by making amorphous metal oxide films by dipping electrodes into a precursor solution and applying an external bias to convert the precursor solution to an amorphous metal oxide. These amorphous metal oxide films may subsequently be tuned by any suitable method, including by annealing as described herein.

In one embodiment, therefore, the present invention provides a method for preparing electrocatalytic materials, comprising coating a substrate with a precursor solution. A precursor solution may include a single metallo-organic precursor or, where a mixed metal oxide film is desired, a mixture of different precursors. Where a mixture of metallo-organic precursors is used, the amount of each precursor in the precursor solution is determined to provide the desired final metal oxide ratios in the resulting catalytic film.

The coating of a substrate with the precursor solution may be achieved by means including, but not limited to, spin coating, dip coating, spray coating, and wiping. After the substrate has been coated with the precursor solution, the coated substrate undergoes a sequence of steps by which the precursor is converted to a metal oxide suitable for electrocatalysis. In this embodiment, the metallo-organic precursor is converted to a zero oxidation state metal. In another embodiment, the precursor solution to the electrocatalyst material does not achieve a zero oxidation state, but the metallo-organic precursor is instead converted to a prepared precursor state metal. The conversion may be achieved by means including, but not limited to, photolysis using visible or UV incident light, irradiation with an electron beam, irradiation with ions, or calcination.

Most metal oxide deposition methods known in the art, such as electro-deposition, liquid phase deposition, sol-gel, chemical vapour deposition, atomic layer deposition, sputtering, pulsed laser deposition, and molecular beam epitaxy, utilize high temperatures or electrical bias and result in thermodynamically stable crystalline forms. The method of the present invention, however, yields stable amorphous thin films distinct from polycrystalline and crystalline films. The amorphous electrocatalytic materials resulting from the present process are not necessarily static and can have a tunable photoresponse and catalytic activity that may be modified in a fashion that is unaccessible to crystalline solids. As a result, the present process provides greater ability to control and manipulate the characteristics of the resulting film. Accordingly, in another embodiment, the present invention provides a method for optimizing or tuning the electronic properties of electrocatalysts of the present invention. The selection or tuning of the properties of the electrocatalytic material may be achieved by means including, but not limited to, annealing at selected temperature, annealing under oxidizing or reducing atmospheres at selected temperatures, or irradiation with an ion beam. In one embodiment, an annealing step is carried out to improve the catalytic properties of the final electrocatalytic material.

As is also demonstrated herein, the catalytic activity of the electrocatalytic materials prepared in accordance with the present invention can be modulated by controlling the combination and relative proportions of the components of the metal oxide mixtures.

Electrocatalytic materials provided by the invention are made of readily-available and/or low-cost material, and are easy to make in mild conditions. Accordingly, the invention lends itself to being mass-producible and commercially competitive in the field of energy capture, storage, and use, as well as oxygen and/or hydrogen production, and/or production of other oxygen and/or hydrogen-containing products.

The system of the present invention provides a means to catalyse (including photocatalysing) the electrolysis (“splitting”) of water by the electrocatalytic material.

The method of the present invention provides a class of electrocatalytic materials that facilitate the production of oxygen and/or hydrogen gas from water at low overpotential. Electrolysis of water, facilitated by the invention, is useful in a wide variety of areas, including in the storage of energy. The invention allows for the facile, low-energy conversion of water to hydrogen gas and/or oxygen gas, where this process can be easily driven by a standard solar panel (e.g., a photovoltaic cell), wind-driven generator, or any other power source that provides an electrical output. The solar panel or other power source can be used to directly provide energy to a user, and/or energy can be stored, via a reaction catalyzed by materials of the invention, in the form of oxygen gas and/or hydrogen gas. In some cases, the hydrogen and oxygen gases may be recombined at any time, for example, using a fuel cell, whereby they form water and release significant energy that can be captured in the form of mechanical energy, electricity, or the like. In other cases, the hydrogen and/or oxygen gases may be used together, or separately, in another process.

Referring to FIG. 1, which depicts a schematic of one embodiment of the method of the present invention, the method involves spincoating a metallorganic precursor solution onto a substrate. The precursor is subsequently photolysed under UV light irradiation. During this process organic ligands are lost as volatile by-products and zero oxidation-state metal or prepared precursor state metal remains on the substrate (Equation 3).

The metal is then readily oxidized in metal oxide by atmospheric oxygen. The resulting film is composed of amorphous metal oxide (Equation 4).

An example of a suitable substrate is fluorine doped tin oxide (FTO) glass, which has a low price and suitable conductive properties. Other suitable substrates include, but are not limited to, indium tin oxide, transparent conducting oxides, semiconducting substrates (e.g. Si, Ge. ZnO), metal surfaces, and conducting plastic.

Precursor Organic Ligand.

The precursor organic ligand of the method of the present invention is photosensitive, in that it may be degraded under UV light. In one embodiment, the organic ligand is chiral, so the precursor film is composed of diastereomeric molecules which do not crystallize. As a result, after photolysis occurs, the deposited material is amorphous. In one embodiment, the precursor is soluble in an organic solvent such as but not limited to hexanes, methyl iso-butyl ketone, acetone, n-butylacetate, toluene, anisole, which has the advantage of being easier to remove than water. In one embodiment, the ligand is an alkanoate, e.g. 2-ethylhexanoate, which is commercially available, relatively inexpensive, possesses an absorption coefficient of approximately 250 nm, and has an unresolved chiral center. It is understood that, under suitable conditions, 2-ethylhexanoate decomposes into volatile byproducts (carbon dioxide, heptane and 2-heptene) according to the following mechanism:

The volatile byproducts are subsequently easily removed from the reaction, leaving a film of metal oxide deposited on the plate which need not be cleaned or purified.

In a further embodiment, the electronic properties of amorphous materials are not necessarily static and can be modified (“tuned”) in a manner that is unaccessible to crystalline solids. PMOD yields stable thin films with photoresponse and catalytic activities that can be tuned by varying the annealing temperature. A person skilled in the art will appreciate other tuning methods are within the scope of the present invention

An annealing step (depicted as “Δ” in FIG. 2) is used to tune the electrochemical properties of the films.

In a further embodiment, the invention provides not only electrocatalytic materials and compositions, but also related electrodes, devices, systems, kits, processes, etc. Non-limiting examples of electrochemical devices suitable for use with the materials provided in accordance with the present invention, including without limitation, electrolytic devices and fuel cells. Energy can be supplied to electrolytic devices by photovoltaic cells, wind power generators, or other energy sources.

The structure of the films was investigated using a variety of techniques. Most films created were amorphous made their analysis less straightforward than if they were crystalline.

Although the compositions, electrodes, systems, and methods described herein are primarily related to water electrolysis (i.e., forming oxygen gas, hydrogen gas, and/or other products from water) and/or the oxidation of hydrogen (e.g., hydrogen gas), the invention is not limited in this way. Where the invention is described as involving a first electrode and/or a second electrode (one or both of which can include an electrocatalytic material), with production of oxygen gas via water electrolysis at the first electrode and/or production of hydrogen gas at the second electrode, it is to be understood that the first electrode can facilitate oxidation of any species, water or otherwise, to produce oxygen gas or another oxidized product. Examples of reactants that can be oxidized in this context can include methanol, formic acid, ammonia, etc. Examples of oxidized products can include CO₂, N₂, etc. At the second electrode, a reaction can be facilitated in which water (or hydrogen ions) is reduced to make hydrogen gas, but it is to be understood that a variety of reactants not limited to water (e.g., acetic acid, phosphoric acid, etc.) can be reduced to form hydrogen gas and any number of other products of the reduction reaction (e.g., acetate, phosphate, etc.). This reaction at the second electrode can be run in reverse, in “fuel cell” operation, such that hydrogen gas (and/or other exemplary products noted above) is oxidized to form water (and/or other exemplary reactants noted above). In some cases, the compositions, electrodes, methods, and/or systems may be used for reducing hydrogen gas. In some cases, the compositions, electrodes, methods, and/or systems may be used in connection with a photoelectrochemical cell. It should be understood that while much of the application herein focuses on the formation of hydrogen and/or oxygen gas from water, this is by no means limiting, and the compositions, electrodes, methods, and/or systems described herein may be used for other purposes, as described herein. Non-limiting examples of electrochemical devices provided by the invention include electrolytic devices and fuel cells. Energy can be supplied to electrolytic devices by photovoltaic cells, wind power generators, or other energy sources. These and other devices are described herein.

DEFINITIONS

Unless defined otherwise, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this invention belongs.

The term “amorphous” as used herein, refers to a material with a disordered atomic-scale structure and no long-range ordering.

The term “electrocatalyst” as used herein, refers to a material that is involved in and increases the rate of a chemical electrolysis reaction (or other electrochemical reaction) and which, itself, undergoes reaction as part of the electrolysis, but is largely unconsumed by the reaction itself, and may participate in multiple chemical transformations. An electrocatalyst may also be referred to as an electrocatalyst composition. It is contemplated that the term electrocatalyst as used herein can include photocatalytic activity.

The term “electrode” as used herein, refers to a solid electric conductor through which an electric current enters or leaves an electrolytic cell or other medium.

The term “electrolysis” as used herein, refers to the use of an electric current to drive an otherwise non-spontaneous chemical reaction. For example, in some cases, electrolysis may involve a change in redox state of at least one species and/or formation and/or breaking of at least one chemical bond, by the application of an electric current. Electrolysis of water, as provided by the invention, can involve splitting water into oxygen gas and hydrogen gas, or oxygen gas and another hydrogen-containing species, or hydrogen gas and another oxygen-containing species, or a combination. In some embodiments, devices of the present invention are capable of catalyzing the reverse reaction. That is, a device may be used to produce energy from combining hydrogen and oxygen gases (or other fuels) to produce water.

The term “chalcogenide” as used herein, refers to a binary compound comprising a chalcogen and a more electropositive element or radical. A “chalcogen” as used herein, refers to the elements oxygen (O), sulfur (S), selenium (Se), tellurium (Te), the radioactive element polonium (Po) and the synthetic element ununhexium (Uuh). Where “chalcogen” and/or “chalcogenide” is used herein to describe what those of ordinary skill in the art would understand to exclude oxygen and oxides, it is to be understood that a chalcogen and/or chalcogenide as defined above is intended.

The use of water as a reactant for catalysis, as referenced herein, is to be understood to mean that the water may be provided in a liquid and/or gaseous state. The water used may be relatively pure, but need not be, and it is one advantage of the invention that relatively impure water can be used. The water provided can contain, for example, at least one impurity (e.g., halide ions such as chloride ions). In some cases, the device may be used for desalination of water. It should be understood that while much of the application herein focuses on the catalytic formation of oxygen gas and hydrogen gas and/or other products from water, this is not limiting, and the compositions, electrodes, methods, and/or systems described herein may be used for other catalytic purposes, as described herein. For example, the compositions, electrodes, methods and/or systems may be used for the catalytic formation of water from oxygen gas.

Electrocatalyst

The present invention relates to an electrocatalyst, a method for preparing the electrocatalyst of the present invention, a system for electrocatalysis, and use of the electrocatalyst in the hydrolysis of water.

The method for preparing the electrocatalyst comprises a thin film deposition technique known in the art of direct lithography in the design of transistors, the Photochemical Metal Organic Deposition (PMOD) technique.

When it is desirable to tune the electronic properties of the electrocatalyst, this may be done by annealing the electrocatalyst film in air at increased temperature.

Electrochemical Devices/Systems

The present invention relates to electrocatalytic materials suitable for use in systems and devices including but not limited to photoelectrochemical cells, (photo)electrocatalytic devices, dye-sensitized solar cells, photovoltaic devices, carbon capture systems, sensors, oil upgrading facilities, chemical production facilities, electrolyzers, desalination systems and devices, water purification systems and devices, and semiconductors.

Electrocatalyst and Related Electrodes

The present invention relates to electrocatalytic materials as electrodes and related electrodes comprising electrocatalytic materials including but not limited to conducting glass substrates, indium-doped tin oxide, and metal substrates (e.g., sheet metal).

To gain a better understanding of the invention described herein, the following examples are set forth. It will be understood that these examples are intended to describe illustrative embodiments of the invention and are not intended to limit the scope of the invention in any way.

EXAMPLES Preparation of Single and Mixed Metal Oxide Films Example 1

The following example describes the preparation of an amorphous iron oxide-based film.

Referring to FIG. 2, substrate covered with a transparent conducting oxide (TCO) is used as a substrate for the film as well as an electrical contact (from the TCO). In this example, in-house cut (ca. 2×2 cm) fluorine-doped tin oxide (FTO; TEC 8; 8 Ωcm²) substrates were successively scrubbed with Alconox™ detergent, sonicated in Alconox™ for 15 min, rinsed with deionized H₂O and sonicated in deionized H₂O and then ethanol for 5 min each, exposed to UV light and O_(3(g)) for 15 min and spin-coated immediately. The precursor, iron (III) 2-ethylhexanoate, was synthesized by adding FeCl₃.6H₂O (1.100 g, 6.84 mmol) and 2-ethylhexanoic acid (3.009 g, 20.59 mmol) to 250 mL of methanol with a stoichiometric amount of KOH (1.285 g, 22.90 mmol). Potassium chloride quickly precipitated out and the solution was isolated through filtration and reduced in volume to give a reddish oil. The oil was then re-dissolved in hexanes and extracted 3 times with distilled water. The hexanes were then dried with magnesium sulfate and the volume of the red solution was reduced in vacuo to give a viscous red-brown oil (2.696 g, 81.2% yield). The molecular composition of the resulting iron (III) 2-ethylhexanoate was determined by mass analysis to be C, 58.35; H, 9.29; N, 0.87; compared to a calculated composition of C, 59.4; H, 9.3; N, 0. Investigation of the ethylhexanoic acid (99.7%, Sigma Aldrich) found a molecular composition of C, 66.34; H, 11.08; N, 0.88; compare to a calculated composition of C, 66.63; H, 11.18; N, 0; thus explaining the presence of nitrogen in the MO, precursor.

Iron(III) 2-ethylhexanoate was dissolved in hexanes (15% w/w). This solution was sonicated 2 min, filtered with a syringe through a 0.2 μm nylon membrane (Life Sciences Acrodisc™), and immediately used. The surface of the clean substrate was saturated with precursor solution and spin-coated (7 sec spread at 1000 rpm, 60 sec spin at 3000 rpm) to yield a thin film of iron(III)-2-ethylhexanoate of optical quality. The coated substrates were subjected to a pre-exposure bake (60° C., 5 min) to remove residual solvent. The coated substrates were exposed to deep-UV light (UVP UVG-54 6 mW low-pressure mercury lamp, λ=254 nm) for 12 hr, under otherwise ambient conditions to induce a photochemically-triggered ligand-to-metal charge-transfer that leads to the destabilization and subsequent decomposition of the complex to yield a Fe₂O₃ film. During this time the film color changed from opaque red/brown to opaque yellow.

A person skilled in the art will appreciate the scope of the present invention includes other organo-metallic solutions are suitable for use as precursor solutions, by way of example, other iron(III)-2-ethylhexanoate solutions including but not limited to commercially available 52% (w/w) iron(III)-2-ethylhexanoate in mineral spirits, which may be diluted before use.

Example 2

In another example, the film of Example 1 is annealed at a temperature chosen from the range of room temperature (i.e. the non-annealed, as-prepared film) to 600° C. for the purpose of selecting properties in the film. The whole PMOD process including annealing is illustrated in FIG. 2.

Example 3a

The films of example 1 were then annealed at different temperatures ranging from no annealing (i.e. not heat-annealed) to 600° C. The films got darker as the annealing temperature increased, indicating a change in structure at a molecular level. Above an annealing temperature of 600° C., the glass substrate started to melt, destroying the samples. The resultant data regarding film characteristics are presented in FIG. 5.

As-prepared films of a-Fe₂O₃ were then annealed in air for 1 h at temperatures ranging between 100° C. and 600° C. FIG. 5 shows the amorphous material is remarkably robust towards crystallization: Bragg peaks due to α-Fe₂O₃ are not observed in the x-ray diffraction patterns until T_(anneal)≧500° C. Even though all of the films annealed at temperatures up to 400° C. are deemed amorphous, the electronic properties of the films are not constant as evidenced by the changing color of the films (FIG. 6) and the disparate absorption coefficients, which are related to the onset of light absorption is pushed further towards lower energies at progressively higher annealing temperatures as shown in FIG. 3). Because X-ray photoelectron spectra confirm that the annealed a-Fe₂O₃ films contain ferric sites exclusively, which is resonant with as-prepared a-Fe₂O₃ and hematite films, as shown in FIG. 22, we ascribe the divergent electronic properties to polyamorphism; i.e., various instances of a structurally disordered material with same composition but different resulting properties. The modification of the material brought on by annealing includes a densification of the material (FIG. 7). At sufficiently high annealing temperatures, the densification process renders a long-range ordered hematite film. The absorption coefficients determined for samples T_(anneal)≧500° C. show signature features of hematite (FIG. 3b ), which is also consistent with the XRD results (FIG. 3a ). Further characterization of the resultant films is discussed below.

Example 3b

In another example, iron and cobalt oxide films were created and the precursor solutions used were respectively 15% and 8% (w/w) in hexane. Both precursors absorbed light at 254 nm. The precursor decomposition was followed using IR spectroscopy, and spectra collected over time are presented in FIG. 4. Photolysis was considered complete when the IR spectrum of the sample looked the same as the spectra of the blank (control) substrate. Both precursors were fully photolysed overnight, i.e. after 16 h of irradiation.

Example 4

In this example, samples of three compositions are prepared from single/binary/ternary solutions of metal 2-ethylhexanoate PMOD precursors. Table 1 lists the specific compositions of the metals precursor solutions. The weight percentage of individual metal precursor is chosen to reflect its solubility in hexane and the optimization in catalytic effects of the resulting MO_(x) film.

TABLE 1 Precursor content (% w/w) Sample Fe(L)₃:Co(L)₂:Ni(L)₂ Fe 15:0:0 FeCo 15:8:0 FeCoNi 15:8:8 FTO substrates were first cut to 2.5×2.5 cm and then sonicated in an Alconox® detergent solution for 15 min, followed by rinsing with deionized H₂O and sonication in deionized H₂O (5 min) and then ethanol (5 min). The substrates were then exposed to the PSD UV3 Ozone Cleaner (Novascan) for 15 min and spin-coated immediately. Metal-organic precursor solutions were prepared by dissolving the calculated amount of different precursors in hexanes to the weight percentage listed in Table 1. The precursor solutions were then spin-coated (7 sec spread at 1000 rpm, 60 sec spin at 3000 rpm) onto the cleaned FTO substrates. The coated substrates were exposed to deep-UV light (UVP UVG-54 6 mW low-pressure mercury lamp) 24 hr to allow a complete conversion of the precursor to the metal oxides. All samples are transparent and homogeneous in appearance.

Characterization of Amorphous Single Metal Oxide Films X-Ray Diffraction and X-Ray Absorption Fine Structure Example 5

The amorphous nature of the as-prepared a-FeO₃ films as prepared, and after annealing at various temperatures were investigated using X-ray diffraction (XRD) studies, using a Rigaku Multiflex θ-2θ diffractometer (scan speed=0.016° min⁻¹, Cu K_(α) tube, λ=1.5406 Å) and baseline-corrected with Jade 6.5 software.

FIG. 5 illustrates the XRD results of Fe₂O₃ films annealed at various temperatures, and confirms the amorphous nature of the films as prepared, and after annealing at up to 400° C. Blank FTO and hematite are provided as reference scans. The onset of the hematite phase for films at T_(anneal)≧500° C. is indicated by the observations of Bragg reflections at 2θ=33.2° and 35.6° which correspond to the (114) and (120) peaks for hematite. The formation of a-Fe₂O₃ is achieved because the photochemical nature of the precursor decomposition bypasses the high temperatures necessary to the formation of crystalline solids thus enabling the kinetic trapping of the metastable amorphous photoproduct. X-ray absorption fine structure (XAFS) studies of as-prepared a-Fe₂O₃ thin films generated by PMOD have confirmed the metal ions to be trivalent, and indicate no long-range order beyond the second nearest neighbor shell.

FTIR Analysis Example 6

Fourier transform infrared spectroscopy (FTIR) was carried out using a Nicolet NEXUS 470 FTIR E.S.P. spectrometer to monitor the photochemical reaction of the precursor film. CsI and KBr IR plates were spin coated with hexanoic solutions varying in amount of precursor (% w/w), and the decomposition of the precursor was monitored by FTIR. FIG. 4 shows the effect of photolysis on the Fe(III) 2-ethylhexanoate precursor on CsI plates by infrared spectroscopy. Spectra (a) represents Blank CsI substrate; (b) Spin-coated film of 2-ethylhexanoic acid on CsI; and (c) Spin-coated solution of 15 w.t. % Fe(III) 2-ethylhexanoate prior to photolysis. The corresponding films were re-analysed after additional photolysis for (d) 2.5 h and (e) 6.3 h at (λ=254 nm). Progressive decrease in absorbance of the C—H and C—O/C═O vibrational modes. ν_(as) and ν_(s) are asymmetric and symmetric stretches, respectively. The signal centred at 1323 cm⁻¹ (not labelled) is a hydrocarbon chain vibrational mode corresponding to 2-ethylhexanoate.

Visual/Optical Characteristics Example 7

Visual characterization of films was carried out on a variety of films. FIG. 6 shows photographs of Fe₂O₃ films annealed at various temperatures. Blank FTO is provided as a reference. The red color of the films becomes more intense at progressively higher annealing temperatures.

UV-visible spectroscopy was performed on both iron and cobalt oxide films. UV/Vis absorbance spectra were collected with a Cary 5000 spectrophotometer (Varian). All spectra were referenced to a blank FTO substrate.

Spectra for iron oxide films are presented in FIG. 15 (a) and spectra for cobalt oxide films are presented in FIG. 15(b). For iron oxide films, the shape of the spectrum changed drastically above 400° C., which was consistent with the structural changes associated with hematite formation. Additionally, the shoulders at 2.3 eV and 3.2 eV are once again characteristic of the formation of a hematite phase. Iron oxide film samples showed a good absorption signal in the visible range, especially the ones annealed at higher temperatures, conforming that this material had the potential to be photocatalytic. On the contrary, cobalt oxide film samples showed a very weak absorbance in the visible light range, precluding their use as photocatalysts. However, a rise in absorption around 1.7 eV were noted for samples annealed above 250° C. These changes, even if much slighter than in the case of the iron oxide films, were attributed to the formation of a crystalline Co₃O₄ phase based the corresponding UV-visible spectra for this material.

FIG. 3b shows the absorbance spectra for iron oxide films as a function of incident wavelength of light. It was also determined that the closest parent crystalline iron oxide is hematite. An examination of the absorption coefficient of the as-prepared a-Fe₂O₃ film shows that significant light absorption is observed only below 500 nm (i.e., >−2.75 eV).

Ultraviolet Photoelectron Spectroscopy (UPS) was used to investigate the position of the valence band of iron oxide materials annealed at different temperatures. UPS ionizes the material surface by removing electrons from the valence band of the sample and monitoring their energy. The valence band positions determined with this technique are shown in FIG. 16, with the corresponding conduction band positions deducted from the Tauc analysis.

A wider difference in energy between the electrolyte and the valence band of the material thermodynamically favours electron transfers from the electrolyte to the material of the metal oxide films. For this reason, amorphous materials showed a better valence band positioning than the crystalline film, which was annealed at 600° C. More precisely, the sample annealed at 250° C. seemed to have the best band positioning for electrocatalysis.

Film Thickness Example 8

Optical Profilometry was used to determine the thickness of the films annealed at various temperatures. The results are shown in FIG. 7. The data demonstrate that higher annealing temperatures yielded thinner films, up to a 600° C. annealing temperature. This was due to an increasing densification of the material with temperature. The sharp drop in thickness between the samples annealed at 500° C. and 600° C. differed from the slow decrease observed at lower temperatures. This was attributed to changes in the structure of the material when annealed at 600° C. The measurements show that the films were ultrathin, with thicknesses in the order of nanometers. Black data points (T_(anneal)≧500° C.) indicate presence of hematite phase. These data indicate a densitification of the amorphous material as it is annealed, which is interpreted as a filling of long-range coordination numbers with nearest-neighbor atomic shells. These values are among the lowest reported in the creation of oxide films. This is due to previously discussed limitations of the photolysis process.

Optical Determination of Band Gaps (E_(g)) Example 9

The Tauc model was developed to parameterize the optical functions of amorphous materials in their interband region. This empirical model takes into account the states present in this region to describe the absorption behaviour of amorphous chalcogenide materials. These additional states create an absorption tail inside the interband region, giving rise to an absorption coefficient behaving differently than in crystalline materials. Tauc, and later Mott and Davis showed that absorption coefficients in amorphous materials followed the relationship: αhν=(hν−E _(g) ^(opt))^(n)  (Equation 7)

where α is the absorption coefficient of the material, h is the Planck constant, ν is the frequency of the incident radiation, K is characteristic constant, is the optical bandgap of the material, and n=½ for indirect transitions, and n=2 for direct transitions.

An absorption coefficient can be derived from absorbance and thickness:

$\begin{matrix} {{A = {\log\left( \frac{I_{0}}{I} \right)}}{I = {I_{0} \times {\mathbb{e}}^{{- \alpha}\; z}}}} & \left( {{Equation}\mspace{14mu} 8} \right) \end{matrix}$

where A is the absorbance, I₀ is the intensity of the incident light, and I is the intensity of the transmitted light. Therefore it follows that:

$\begin{matrix} {\alpha = {\frac{A}{z} \times \ln\; 10}} & \left( {{Equation}\mspace{14mu} 9} \right) \end{matrix}$

The thin films were subjected to UV-visual light absorption analysis, where E_(g) can be obtained using Tauc's formula, according to Equation 7 above. (A=absorption coefficient; n=0.5 for direct transitions; n=2 for indirect transitions). FIG. 8 illustrates the energy intercept of the plots, with FIG. 8(a) and FIG. 8(b) demonstrating the direct and indirect bandgaps, respectively. Direct and indirect E_(g) values were determined in FIG. 8(c) from energy intercepts of the fitted black lines in FIGS. 8(a) and 8(b), respectively. Data points at annealing temperatures at and above 500° C. indicate presence of hematite phase.

Scanning Electron Microscopy Example 10a

Morphological characterization was carried out with scanning electron microscopy (SEM) using a tungsten-filament SEM (FEI XL 30, accelerating voltage 20 kV).

FIG. 9 shows the electron micrographs of blank FTO and Fe₂O₃ films annealed at various temperatures. The films are featureless and conform to the substrate. Cracking due to poor adhesion with the FTO surface occurs after photolysis; this feature is common in all annealed films.

X-Ray Photoelectron Spectroscopy (XPS) Example 10b

XPS spectra of Fe₂O₃ films as-prepared and annealed at various temperatures were obtained by irradiating the films under ultra high vacuum with a beam of X-rays while simultaneously measuring the kinetic energy and number of electrons that escape from the top 1 to 10 nm of the films. Results are shown in FIG. 22.

A PHI VersaProbe 5000-XPS was used to record XPS spectra using a monochromatic Al source, 1486.6 eV, at 49.3 W and beam diameter of 200.0 μm. For each sample, a high sensitivity mode spectrum was taken with a wide binding energy range of 0-1,350 eV to determine the surface elemental composition of the samples. Legend denotes the annealing temperature for respective films. High resolution XPS spectra of the Fe2p_(1/2) and Fe2p_(3/2) regions of the as-prepared sample (Fe2p_(1/2)=724.32 Fe2p_(3/2)=710.11) and samples annealed at 250° C. (Fe2p_(1/2)=724.15 Fe2p_(3/2)=710.58) and 600° C. (Fe2p_(1/2)=724.15 Fe2p_(3/2)=710.60) are consistent with Fe₂O₃ (Fe2p_(1/2)=724.40 Fe2p_(3/2)=710.95).

Electrocatalytic Properties of Single and Mixed Metal Oxide Films

The potential of single and mixed metal oxides as being electrocatalytic for oxygen evolution has been investigated using a variety of electrochemical measurements: cyclic voltammetry, Tafel analysis of photocatalysis at various over potentials and Mott-Schottky analysis of flat band potential.

Current Density as a Function of Annealing Temperature Example 11

Resultant current density of electrolytic cells constructed with Fe₂O₃ films was measured at 0.1 M NaOH(aq) using an applied potential of 1.53 V vs. RHE. Electrochemical data were obtained by cyclic-voltammetry using a three-electrode cell and a scanning potentiometer (Princeton Applied Research Versastat 3). Reference electrodes for measurement in 1.0 M NaOH_((aq)) (pH=13.6) and 0.1 M NaOH_((aq)) (pH=13.0) were Hg/HgO fitted with polyethylene frits (Koslow Scientific) and filled with 1.0 M NaOH(aq) and 0.1 M NaOH(aq) respectively. Measurements in 0.1 M KNO_(3(aq)) were performed with a Ag/AgCl reference electrode filled with saturated KCl(aq). Potentials reported herein are referenced to a reversible hydrogen electrode (RHE, V_(RHE)=0.000−0.0591·pH). The catalytic anode was the working electrode and it had a platinum counterelectrode.

FIG. 12 depicts the current density for iron oxide films, and demonstrates the superior activities of the films annealed over the 200-300° C. range. Data points at annealing temperatures of 500° C. and higher indicate presence of hematite phase.

Cyclic Voltammetry Example 12

Cyclic voltammetry experiments were run on cobalt and iron oxide films in 0.1M sodium hydroxide. Voltage was applied against a reference electrode such as Ag/AgCl or Hg/HgO, and reported against the reversible hydrogen electrode (RHE) in a linear sweep between 0.4V and 1.7V, and resulting output intensity (overpotential) was measured. Results are depicted in FIG. 18.

Voltammograms for iron oxide films showed the same shape irrespective of the annealing temperature: one reductive wave around 0.4 V vs RHE, attributed to a Fe(III)/Fe(II) couple, and one couple located at the onset of catalysis, attributed to a Fe(IV)/Fe(III) couple.

Analysis of cobalt oxide films resulted in different voltammogram shape depending on whether they were annealed above or below 200° C. Cobalt oxide films annealed below 200° C. presented three reversible couples (with an oxidative wave and a reductive wave): one around 1.1 V vs RHE (I), one around 1.2 V vs RHE (II) and one around 1.5 V vs RHE(III). Cobalt oxide films annealed above 200° C. presented only a reductive wave around 0.6 V vs RHE (IV) and a reversible couple around 1.5 V vs RHE (V). This difference was consistent with the differences seen in UV-visible spectra and sample colors, and confirmed that a new oxide structure arises when the film is annealed above 200° C. Cyclic voltammograms for samples annealed below 200° C. were consistent with the ones reported for amorphous cobalt oxide electrochemically deposited. Couple I would then correspond to the equilibrium between Co(OH)₂ and Co₃O₄, couple II to the one between Co(OH)₂ or Co₃O₄ and CoOOH, and couple III to the one between CoOOH and CoO₂. This last species was the one from which oxygen was evolved. On the other hand, there was only one reversible couple before the catalytic onset for samples annealed above 200° C. This could once again be consistent with a crystalline Co₃O₄ material, where couple V would correspond to its equilibrium with CoOOH, and wave IV would be its reduction into Co(OH)₂. The +IV oxidation state formation would then be hidden by the catalytic onset. To summarize, it seemed that catalytic species were at +IV oxidation level in every case.

Amorphous iron oxide films had earlier onsets in terms of potential (see FIG. 10), demonstrating better activity as electrocatalysts than the crystalline iron oxide films. For the cobalt oxide films, the onset potential was not clearly defined, due to the presence of reversible couples in the same region.

FIG. 10 shows the cyclic voltammetry data recorded in 0.1 M NaOH(aq) (pH=12.9) at a scan velocity ν=50 mV s⁻¹ for films annealed at various temperatures, highlighting the differences in catalytic activities between the most active amorphous a-Fe₂O₃ film, hematite, and a blank FTO substrate.

FIG. 23A shows the cyclic voltammetry data recorded for iridium oxide and iron oxide containing iridium films annealed at various temperatures, highlighting the differences in catalytic activities between the samples annealed at 300° C. which show optimized catalytic activity, and the as-prepared and 600° C. annealed films.

FIG. 23B shows the cyclic voltammetry data recorded for molybdenum oxide films produced using three different annealing temperatures, and molybdenum doped iron oxide films produced at three different annealing temperatures, highlighting the differences in catalytic activities between the samples annealed at 300° C. which show optimized catalytic activity, and the as-prepared and 600° C. annealed films. Cyclic voltammetry data recorded for bare FTO electrode (annealed at 300° C.) and iron oxide film (as-prepared) are also included for reference.

FIG. 23C shows the cyclic voltammetry data recorded for niobium oxide films produced using three different annealing temperature, and niobium doped iron oxide films produced at three different annealing temperatures. Cyclic voltammetry data recorded for bare FTO electrode (annealed at 300° C.) and iron oxide film (as-prepared) are also included for reference.

Tafel Plots Example 13

The electrocatalytic behavior of the samples for water oxidation is demonstrated by measuring the current densities as a function of the overpotential (η) in 0.1 M NaOH electrolyte, as is shown in FIG. 24, which shows Tafel plots determined in 0.1 M NaOH (pH=12.9). In this figure, overpotential η=(V_(appl)−iR)−E (pH 12.9), where V_(appl) is the applied potential vs. NHE, iR denotes the internal voltage drop in the solution and E (pH 12.9) is the anodic potential for oxygen evolution at pH 12.9, namely (1.23−0.059×12.9) V vs NHE, respectively.

Iron oxides are known to exhibit high values when they catalyze oxygen evolution reactions (OERs), as is the case here for Sample Fe consisting of pure amorphous iron oxide. Appreciable catalytic current is seen only at η>0.4 V, and a benchmark of 1 mA cm⁻² cannot be observed up to a η of 0.45 V. The low catalytic activity of pure iron oxide in OER can be possibly rationalized by the formation of unstable surface species of higher oxygen coordination number that trigger oxygen evolution on the iron oxide and/or slow hole transfer kinetics at the iron oxide-electrolyte interface.

Addition of Co and/or Ni to the amorphous iron oxide greatly improves the performance of the OER catalysis. For example, compared to Sample Fe, Sample FeCo reduces η by around 160 mV at the same oxygen evolution current density. The catalytic activity of the electrode is further enhanced by incorporating Ni in the oxide mixture (Sample FeCoNi), rendering a η of 0.25 V at a current density of 1 mA cm⁻².

For comparison, a bare FTO electrode was used as a control and its Tafel plot in the same electrolyte is plotted against Sample Fe in FIG. 25. It is apparent that F-doped tin oxide demonstrates a very low catalytic activity for water oxidation, excluding any current density contributions from FTO glass substrate in the overpotential range of 0.2 to 0.5 V presented in FIG. 24.

Example 14

The catalytic activity of Sample FeCoNi was also tested under neutral conditions and the Tafel plot is shown in FIG. 26, which shows a Tafel plot for FeCoNi in 0.5 M KPi solution (pH=7.0) and natural seawater (pH=8.4, from Vancouver, British Columbia) corrected for IR drop across the solution. The amorphous nature and/or the composition of the oxides were not compatible with the 0.5 M KPi buffer solution and Sample FeCoNi was found to dissolve in the neutral condition due to the poor adhesion of the film to the FTO substrate. Nonetheless, this was alleviated by simply annealing the film (300° C., in air, 1 hr), which greatly improved the durability of the FeCoNi film to the FTO substrate at neutral conditions, while retaining the amorphous nature of the film. Compared to the value in 0.1 M NaOH, FeCoNi shows a higher overpotential of −230 mV to 0.48 V at a same oxygen evolution current density of 1 mA cm⁻². FIG. 26 also shows that FeCoNi retains a moderate performance in natural seawater (pH 8.4, from Vancouver, British Columbia, 49° 18′ N, 123° 6′ W) and increases by around 200 mV at the same oxygen evolution current density, as is noticed in another Co-OEC catalyst system.¹² The lower catalytic activity of FeCoNi in seawater might be due to the low conductivity of the seawater and could be potentially reduced by adding electrolytes, such as KOH, KPi or KBi to the solution.

Example 15

The electrocatalytic behavior for water oxidation of the binary and ternary metal oxides listed in Tables 2 and 3 was determined using the same protocol set out in Example 13 above, with the exception that all measurements were performed in aqueous 0.1 M KOH. As these materials are amorphous metal oxides, the oxygen content is not accurately known, and is omitted for clarity in Tables 2 and 3.

TABLE 2 Catalytic Onset Overpotential Tafel Slope Binary, Amorphous V mV dec⁻¹ Metal Oxide Composition Average St. Dev. Average St. Dev. Fe 0.37 0.02 40 4 Fe₂₀Co₈₀ 0.27 0.02 37 4 Fe₄₀Co₆₀ 0.25 0.02 34 3 Fe₆₀Co₄₀ 0.25 0.02 40 7 Fe₈₀Co₂₀ 0.24 0.02 43 9 Co 0.26 0.02 42 2 Fe₈₀Ni₂₀ 0.27 0.03 33 3 Fe₆₀Ni₄₀ 0.26 0.01 31 3 Fe₄₀Ni₆₀ 0.25 0.01 34 8 Fe₂₀Ni₈₀ 0.23 0.01 46 12 Ni 0.25 0.01 73 6 Co₂₀Ni₈₀ 0.25 0.01 80 7 Co₄₀Ni₆₀ 0.25 0.01 73 6 Co₆₀Ni₄₀ 0.23 0.01 60 2 Co₈₀Ni₂₀ 0.23 0.01 63 3 Co₈₀Al₂₀ 0.26 0.01 42 1 Co₆₀Al₄₀ 0.27 0.01 46 3 Co₄₀Al₆₀ 0.27 0.01 44 3 Co₂₀Al₈₀ 0.27 0.01 39 1 Ni₈₀Al₂₀ 0.28 0.02 61 1 Ni₆₀Al₄₀ 0.26 0.01 30 3 Ni₄₀Al₆₀ 0.3 0.01 51 7 Ni₂₀Al₈₀ 0.29 0.01 12 2 Fe₈₀Al₂₀ 0.31 0.02 32 6 Fe₆₀Al₄₀ 0.31 0.02 37 1 Fe₄₀Al₆₀ 0.3 0.01 36 4 Fe₂₀Al₈₀ 0.29 0.01 34 4 Al 0.4 0.08 89 19 Fe₉₈Ce₂ 0.32 0.01 40 4 Fe₉₅Ce₅ 0.32 0.01 32 1 Fe₉₀Ce₁₀ 0.33 0.01 32 1 Fe₈₀Ce₂₀ 0.33 0.02 32 1 Fe₇₀Ce₃₀ 0.32 0.01 36 1 Fe₆₀Ce₄₀ 0.32 0.01 37 2 Fe₅₀Ce₅₀ 0.31 0.01 40 2 Ce 0.38 0.01 72 15 Fe₈₀Mo₂₀ 0.32 0.01 43 2 Fe₆₀Mo₄₀ 0.33 0.01 46 1 Fe₄₀Mo₆₀ 0.33 0.01 49 3 Mo 0.35 0.03 58 9 Fe₈₀Cu₂₀ 0.29 0.01 42 4 Fe₆₀Cu₄₀ 0.29 0.01 46 4 Fe₄₀Cu₆₀ 0.3 0.02 50 15 Fe₂₀Cu₈₀ 0.31 0 45 5 Cu 0.33 0.02 54 14 Fe₈₀Ir₂₀ 0.21 0.01 50 2 Fe₆₀Ir₄₀ 0.21 0.01 44 3 Fe₄₀Ir₆₀ 0.2 0.01 41 1 Fe₂₀Ir₈₀ 0.22 0.01 44 4 Ir 0.21 0.01 80 13 Fe_(99.5)Mn_(0.5) 0.38 0.04 32 7 Fe₉₈Mn₂ 0.38 0.01 33 5 Fe₉₆Mn₄ 0.37 0.01 32 3 Fe₉₄Mn₆ 0.37 0.01 33 4 Fe₉₂Mn₈ 0.36 0.03 35 5 Fe₉₀Mn₁₀ 0.36 0.01 34 2 Fe₈₀Mn₂₀ 0.36 0.02 37 4 Fe₆₀Mn₄₀ 0.35 0.01 46 2 Fe₄₀Mn₆₀ 0.35 0.02 42 3 Mn 0.5 0.01 55 4 Fe_(99.5)Sn_(0.5) 0.39 0.03 57 7 Fe₉₈Sn₂ 0.33 0.01 48 15 Fe₉₆Sn₄ 0.37 0.01 35 4 Fe₉₄Sn₆ 0.38 0.02 42 5 Fe₉₂Sn₈ 0.39 0.02 33 2 Fe₉₀Sn₁₀ 0.39 0.01 35 3 Fe_(99.5)Nb_(0.5) 0.38 0.02 39 2 Fe₉₈Nb₂ 0.4 0.01 47 3 Fe₉₆Nb₄ 0.4 0.03 49 4 Fe₉₄Nb₆ 0.39 0.01 48 5 Fe₉₂Nb₈ 0.41 0.02 55 3 Fe₉₀Nb₁₀ 0.41 0.01 41 3

TABLE 3 Catalytic Onset Overpotential Tafel Slope Ternary, Amorphous V mV dec⁻¹ Metal Oxide Composition Average St. Dev. Average St. Dev. Fe₂₀Co₂₀Ni₆₀ 0.23 0.01 52 5 Fe₂₀Co₄₀Ni₄₀ 0.23 0 49 4 Fe₂₀Co₆₀Ni₂₀ 0.23 0.01 47 5 Fe₄₀Co₂₀Ni₄₀ 0.23 0.01 43 1 Fe₄₀Co₄₀Ni₂₀ 0.24 0 40 1 Fe₆₀Co₂₀Ni₂₀ 0.25 0 39 2 Fe₂₀Al₂₀Ni₆₀ 0.27 0.01 20 2 Fe₂₀Al₄₀Ni₄₀ 0.3 0.02 9 2 Fe₂₀Al₆₀Ni₂₀ 0.3 0.01 12 2 Fe₄₀Al₂₀Ni₄₀ 0.3 0.01 16 1 Fe₄₀Al₄₀Ni₂₀ 0.31 0.01 23 3 Fe₆₀Al₂₀Ni₂₀ 0.32 0.01 27 1 Al₂₀Co₂₀Ni₆₀ 0.3 0.01 60 1 Al₂₀Co₄₀Ni₄₀ 0.27 0.01 52 1 Al₂₀Co₆₀Ni₂₀ 0.26 0.01 49 2 Al₄₀Co₂₀Ni₄₀ 0.28 0 57 1 Al₄₀Co₄₀Ni₂₀ 0.27 0.01 50 2 Al₆₀Co₂₀Ni₂₀ 0.28 0 52 2 Al₂₀Co₂₀Fe₆₀ 0.27 42 Al₂₀Co₄₀Fe₄₀ 0.26 36 Al₂₀Co₆₀Fe₂₀ 0.25 35 Al₄₀Co₂₀Fe₄₀ 0.28 47 Al₄₀Co₄₀Fe₂₀ 0.26 32 Al₆₀Co₂₀Fe₂₀ 0.26 39

The above data suggest some general trends. For example, addition of Fe tends to improve the Tafel slopes (catalytic performance) of other metal oxides. For example, amorphous NiO_(x) exhibits a Tafel slope of 73+/−6 mV dec⁻¹. Addition of Fe to the catalyst results in slopes better than 40 mV dec⁻¹ (e.g. 31 mV dec⁻¹ for Fe₆₀Ni₄₀O_(x)). Also, when starting from FeO_(x), the addition of more electron rich elements (Co, Ni, Cu, Al, Ir) results in significant decreases in activation overpotential, and the addition of more electron deficient elements (Mo, Mn, Nb) results in small, but measurable decreases in activation overpotential. Iron can also be added to promising ternary catalysts to further improve their behavior, e.g., Ni₆₀Al₄₀O_(x) produced an activation overpotential of 0.26 V and a Tafel slope of 30 mV dec⁻¹, but addition of Fe to the sample Fe₂₀Al₂₀Ni₆₀O_(x) produced an activation overpotential of 0.27 V and a slope of 20 mV dec⁻¹.

In addition, aluminum appears to be a promising additive to further improve Tafel slopes, e.g., Fe₂₀Al₄₀Ni₄₀ has a Tafel slope of 9 mV dec-1, and several other Al-containing catalysts exhibit slopes better than 15 mV dec-1.

Electrochemical Impedance Spectroscopy Analysis Example 16

The AC impedance measurements of the Fe₂O₃ films were recorded with a potentiostat/galvanostat (Gamry EIS 300 with onboard controller PCI4G300-49085 using Gamry Instrument Framework 5.61). The applied bias voltage was varied vs. the reference electrode and the ac amplitude rms was 10 mV between the Pt counter electrode and the FTO/Fe₂O₃ working electrode. The frequency range explored was 0.1 to 1000 Hz. The following relationship was used to build Mott-Schottky plots for each sample (Equation 10):

$\frac{1}{C^{2}} = {\frac{2}{ɛ\; ɛ_{0}A^{2}{eN}_{D}}\left( {V - V_{fb} - \frac{k_{B}T}{e}} \right)}$

Where C represents the capacitance, e is the dielectric constant of iron oxide (12.5),¹⁰⁷ ∈₀ is the dielectric constant of a vacuum (8.854×10⁻¹⁴ C·V¹·cm⁻¹), A is the area of the film in cm, e is the electronic charge (1.602×10⁻¹⁹ C), N_(D) is the donor density (cm⁻³), k_(B) is Boltzmann's constant (1.380×10⁻²³ J·K⁻¹), T is the temperature dependence of the plot, V_(fb) the flat band potential (V) and V is the applied potential (V). Potentiostatic impedance at 1000 Hz performed at voltages ranging from 0 to 1.1 V vs RHE gave a series of Nyquist plots which were fitted with the simple circuit:

The C_(b) values were plotted against the applied voltage to give Mott-Schottky plots shown in FIG. 13a . The space charge capacitance vs. electrode potential for the Fe₂O₃ thin film annealed at 500° C. shows the determination of the flat band potential (V_(fb)) and majority charge carrier density (N_(D)). All of the Fe₂O₃ thin films in this study show a positive slope in the Mott-Schottky plots, indicating n-type semiconductor properties, irrespective of annealing temperature.

The data in the Mott-Schottky plot is then used to derive the majority charge carrier density (N_(D)) in 0.1 M NaOH and 0.1 M KNO₃, as shown in FIG. 13b , to compare solvent effects. Donor densities of the Fe₂O₃ films are on the same order of magnitude, as determined from the Mott Schottky plots. Disparate catalytic activities are therefore not ascribed in any significant manner to a modulation of the charge carrier concentrations. Annealing temperatures of 500° C. or greater indicate presence of hematite phase.

Photocatalytic Activity of the Electrocatalyst Example 17

The electrocatalytic activity, namely the hydrolysis of water, was evaluated by fluorimetry. Measurement of dioxygen production evolution were monitored every 10 s with an optical probe (Ocean Optics FOXY-OR125-AFMG) and a multifrequency phase fluorimeter (Ocean Optics MFPF-100). Raw data from the sensor was collected by the TauTheta Host Program and then converted into calibrated O₂ sensor readings in “% O₂” by the Ocean Optics I Sensors application.

FIG. 11 shows the evolution of dioxygen during controlled-potential electrolysis using an a-Fe₂O₃ sample annealed at 250° C. on FTO. Catalytic wave generation of dioxygen was confirmed by spectroscopically monitoring dioxygen evolution with a fluoroescence optical probe at an applied potential of 2.0 V vs. RHE in 1.0 M NaOH(aq).

Example 18

Photocatalytic studies were performed on iron oxide films. Four different films were tested: a film composed of 5 layers of amorphous iron oxide annealed at 250° C. (sample A1); a film composed of 5 layers of amorphous iron oxide annealed at 400° C. (sample A2); a film composed of 5 layers of crystalline iron oxide annealed at 600° C. (sample C); a film composed of 4 layers of crystalline iron oxide annealed at 600° C. and one layer of amorphous iron oxide annealed at 250° C. on top of them (sample CA).

Cyclic voltammetry and chronoamperometry experiments were then performed on the films, in the dark and under a one sun equivalent of illumination.

Cyclic voltammograms were acquired in 0.1 M NaOH. For amorphous films A1 and A2, no clear difference appeared between the voltammograms acquired in the dark and under illumination. Samples C and CA, an additional anodic current appeared when the sample was exposed to light, indicating that a photoelectrochemical process was taking place at the film surface. Cyclic voltammetry results are presented in FIG. 19.

Chronoamperometry data obtained for CA sample at 1.53V versus RHE are shown in FIG. 20 and data obtained for each sample at the same voltage are shown in FIG. 21. Samples C and CA demonstrate a rise in current when under illumination, demonstrating photocatalytic behaviour. Amorphous samples A1 and A2 gave lower photocurrents. Current density values produced by each sample at 1.23V, 1.53V and 1.73V versus RHE are compiled in FIG. 21.

Example 19

As shown in FIG. 27, the production of O₂ was confirmed by the evolution of O₂ bubbles off the anode immediately after the start of chronoamperometry experiments at η=0.5V, 0.7 V and 1.3V. O₂ production amount measured by fluorescent sensor (red dots) and theoretical amount of O₂ produced (black line) based on a Faradaic efficiency of 100%. As shown in FIG. 27a , electrolysis was carried out in 0.1 M NaOH at a η=0.5 V, i.e. a potential of 0.97 V vs NHE. As shown in FIG. 27b , electrolysis was carried out in 0.1 M NaOH at a η=0.7 V, i.e. a potential of 1.17 V vs NHE. As shown in FIG. 27c , electrolysis was carried out in 0.1 M NaOH at a η=1.3 V, i.e. a potential of 1.77 V vs NHE.

The Faradaic efficiency of the FeCo oxide catalyst was measured with a fluorescence-based O₂ sensor. The experimentally found O₂ amount is plotted against experimental time, together with the theoretical values of O₂ evolution amount based on a Faradaic efficiency of unity (FIG. 27). After passing a charge of 30 C through the anode, 76 μmol O₂ were generated in the system, consistent with the expected amount of 78 μmol, confirming a Faradaic efficiency close to 100%. Measurements of dioxygen evolution were monitored every 10 s with an optical probe (Ocean Optics FOXY-OR125-AFMG) and a multifrequency phase fluorimeter (Ocean Optics MFPF-100). Raw data from the sensor was collected by the TauTheta Host Program and then converted into the appropriate calibrated O₂ sensor readings in “% O₂” by the OOISensors application.

Other Embodiments

Although the invention has been described with reference to certain specific embodiments, various modifications thereof will be apparent to those skilled in the art without departing from the spirit and scope of the invention. All such modifications as would be apparent to one skilled in the art are intended to be included within the scope of the following claims. 

We claim:
 1. An electrocatalytic material comprising an amorphous metal oxide film, wherein said metal oxide is a single metal oxide selected from oxides of iron, cobalt, nickel, ruthenium, platinum, palladium, molybdenum, osmium, manganese, chromium, rhodium, and iridium, or said metal oxide is a mixed metal oxide comprising two or more metals, at least one of which is selected from iron, cobalt, nickel, ruthenium, platinum, palladium, molybdenum, osmium, manganese, chromium, rhodium, and iridium.
 2. The electrocatalytic material of claim 1, wherein the amorphous metal oxide film comprises a metal oxide selected from the group consisting of iron oxide, ruthenium oxide, cobalt oxide, nickel oxide, iridium oxide and mixtures thereof.
 3. The electrocatalytic material of claim 1, wherein the amorphous metal oxide film comprises a binary metal oxide system, wherein the binary metal oxide system is selected from the group consisting of iron/cobalt, iron/nickel, cobalt/nickel, cobalt/aluminum, nickel/aluminum, iron/aluminum, iron/cerium, iron/molybdenum, iron/copper, iron/iridium, iron/manganese, iron/tin, and iron/niobium.
 4. The electrocatalytic material of claim 1, wherein the amorphous metal oxide film comprises a ternary metal oxide system, wherein the ternary metal oxide system is selected from the group consisting of iron/cobalt/nickel, iron/aluminum/nickel, aluminum/cobalt/nickel, and aluminum/cobalt/iron.
 5. The electrocatalytic material of claim 1, wherein the amorphous metal oxide film comprises a doped metal oxide selected from the group consisting of iridium doped iron oxide, niobium doped iron oxide and molybdenum doped iron oxide.
 6. A system for electro catalysis comprising an electrocatalytic material as defined in claim
 1. 